Perpendicular magnetic recording medium for high density recording and manufacturing of the same

ABSTRACT

Embodiments of the invention provide a medium which provides high media S/N and good corrosion resistance. According to one embodiment, in a perpendicular magnetic recording medium at least comprising a soft-magnetic underlayer, a seed layer, an intermediate layer, a magnetic recording layer and an overcoat layer which are stacked over a substrate in order, the magnetic recording layer has a granular structure which consists of many columnar grains of CoCrPt alloy and a grain boundary layer containing an oxide, the seed layer is made of TaNi alloy or TaTi alloy and the intermediate layer is made of Ru or Ru alloy which contains about 80 at. % Ru or more.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application claims priority from Japanese Patent Application No.JP2004-359868, filed Dec. 13, 2004, the entire disclosure of which isincorporated herein by reference.

BACKGROUND OF THE INVENTION

The present invention relates to a magnetic recording medium which canrecord a large volume of data and a method of manufacturing the same,and more particularly to a magnetic recording medium which is suitablefor high density magnetic recording.

As can be understood from the recent tendency that not only personalcomputers but also home electric appliances incorporate compactlarge-capacity magnetic disk devices, demand for a larger capacitymagnetic storage is growing and improvement in recording density isexpected. In order to cope with this, efforts to develop new magneticheads and magnetic recording media have been vigorously made. However,it is difficult to improve the recording density using the currentcommercial longitudinal magnetic recording system. Therefore, researchhas been made on perpendicular magnetic recording as an alternative tothe longitudinal recording system. Perpendicular recording is consideredto be essentially suitable for high density recording becauseneighboring magnetizations do not face each other and the condition ofhigh density recording is stable. Also, a combination of a single poletype recording head and a double-layered perpendicular magneticrecording medium with a soft-magnetic underlayer can improve thewritability and cope with an increase in coercivity of recording layer.However, it is necessary to achieve low media noise performance and highthermal stability in order to realize high density recording based onthe perpendicular recording system.

For the recording layer of a perpendicular magnetic recording medium,research has been made on the use of CoCrPt alloy film which has beenused for longitudinal magnetic recording media. In order to achieve lowmedia noise performance using CoCrPt alloy film, Cr segregation tocrystal grain boundaries must be used to reduce exchange couplingbetween magnetic crystal grains and make the magnetic reversal unitsmaller. However, if the quantity of Cr is insufficient, low noisecharacteristic is not obtained since the insufficient Cr makes grainsunite and become larger in the course of recording layer forming processor the decrease of exchange coupling among grains is insufficient. Onthe other hand, if the amount of Cr is large, much Cr remains in grainsand the magnetic anisotropy energy of magnetic grains declines andsatisfactory thermal stability cannot be attained.

In order to solve this problem and achieve low media noise performance,for example, as disclosed in JP-A No. 178413/2003, many studies havebeen made on a granular type recording layer of oxide-added CoCrPtalloy. When a granular type recording layer is employed, magneticintergrain exchange coupling is reduced by forming an oxide grainboundary layer which surrounds magnetic grains and thus a CoCrPt alloymaterial with a high magnetic anisotropy energy may be used regardlessof the Cr concentration. Also, since the oxide grain boundary layer isdiscontinuous with magnetic grains in terms of crystal and has somethickness, amalgamation of grains hardly occurs in the process offorming a recording layer. For this reason, a granular typeperpendicular magnetic recording medium of oxide-added CoCrPt alloy isattracting attention as a candidate for a low-noise and thermally stableperpendicular magnetic recording medium. So far many researches havebeen made on the seed layer and intermediate layer of a perpendicularmagnetic recording medium. For example, JP-A No. 162807/2003 disclosesseed layers of B, C, Al, Si, P, Ti, Zr, Hf, Cr, V, Nb, Ta, Ru, Rd, Pd,Pt, Cu, Ag and Au, and NiAL and NiTa which combine these with a magneticmetal Fe, Co or Ni, and intermediate layers of Co, Cr, Pt, Pd, Rh and Rualloy. In addition, it is reported, for example, in IEEE Transactions onMagnetics, Vol. 38, No. 5, p. 1976 (2002) that Ru is suitable forintermediate layers of oxide granular type perpendicular magneticrecording media. Also, it is reported, for example, in IEEE Transactionson Magnetics, Vol. 38, No. 5, p. 1979 (2002) that a Ta seed layerimproves the crystal grain alignment of a Ru intermediate layer.

BRIEF SUMMARY OF THE INVENTION

So far, although studies have been made on the noise characteristic andthermal stability of an oxide granular type perpendicular magneticrecording medium, its corrosion resistance has not been studiedsufficiently. We conducted a corrosion resistance test on oxide granulartype perpendicular magnetic recording media which use a Ta seed layerand a Ru intermediate layer and provide a high media S/N, and many pitcorrosions were observed and it has been found that they had the problemof corrosion resistance. When non-magnetic CoCr alloy well known as amaterial for the intermediate layer of the conventional longitudinalmagnetic recording medium was used for the intermediate layer instead ofRu, corrosion resistance was improved but the media S/N drasticallydeclined. In short, it has been found that the combination of theconventional known intermediate layer material and seed layer materialcannot provide both high media S/N and corrosion resistance.

A feature of the present invention is to realize a perpendicularmagnetic recording medium with a granular type recording layer ofoxide-added CoCrPt alloy which provides both high media S/N and goodcorrosion resistance, by selective combination of intermediate layer andseed layer materials and structures.

According to one aspect of the present invention, in a perpendicularmagnetic recording medium at least comprising a soft-magneticunderlayer, a seed layer, an intermediate layer, a magnetic recordinglayer and an overcoat layer which are stacked over a substrate in order,the magnetic recording layer has a granular type structure whichconsists of many columnar grains of CoCrPt alloy and a grain boundarylayer containing an oxide, the seed layer is made of TaNi alloy or TaTialloy and the intermediate layer is made of Ru or Ru alloy whichcontains 80 at. % Ru or more. The granular type perpendicular magneticrecording medium in the present invention provides high media S/N andgood corrosion resistance through a combination of a TaNi alloy or TaTialloy seed layer and a Ru or Ru alloy intermediate layer. When theintermediate layer, which is in contact with the seed layer, is made ofRu or Ru alloy with high crystal grain alignment, better corrosionresistance can be achieved. This perpendicular magnetic recording mediumis characterized in that full width at half-maximum Δθ₅₀ of the Rockingcurves of the Ru (0002) diffraction peak measured with X-ray diffractionis about 4 degrees or less. In addition, it is desirable that the seedlayer is made of TaNi alloy which contains Ni in the range from about 20at. % to 80 at. % or TaTi alloy which contains Ti in the range fromabout 10 at. % to 40 at. %.

For improvement in the corrosion resistance of a perpendicular magneticrecording medium, it may be effective to use a corrosion resistantmaterial for each layer of the medium. However, it has been found thateven when materials with equal corrosion resistance are used, themedium's corrosion resistance considerably differs. As a result ofdetailed examinations, it has been found that the combination ofmaterials rather than the corrosion resistance of each materialinfluences the medium's corrosion resistance. The electrical andchemical properties and adhesion between materials are thought to beimportant factors which determine the corrosion resistance. For adhesionbetween materials, not only the combinations of materials but alsocrystallinity are thought to be important factors. The present inventionis characterized by achieving good corrosion resistance through acombination of TaNi alloy or TaTi alloy and Ru and is based on thefinding that control of crystal grain alignment of Ru is important.

On the other hand, in order to achieve high media S/N, the surfaceroughness of the intermediate layer on the recording layer side must beincreased to promote oxide segregation to grain boundaries of themagnetic recording layer. In short, in order to achieve both high mediaS/N and good corrosion resistance at the same time, it is necessary touse an intermediate layer which is good in crystal grain alignment andhas an enough surface roughness. For realization of such an intermediatelayer, in a method of manufacturing a perpendicular magnetic recordingmedium in the present invention, a lower intermediate layer and an upperintermediate layer are stacked by different deposition conditions toconstitute an intermediate layer of Ru or Ru alloy and the gas pressurefor forming the upper intermediate layer is higher than that for formingthe lower intermediate layer. It is desirable that the gas pressure forforming the lower intermediate layer is in the range from about 0.3 Pato 1 Pa. Instead of using different gas pressures for forming the lowerand upper intermediate layers, different deposition rates may be used toproduce a similar effect. If that is the case, the lower intermediatelayer should be made at a higher deposition rate than the upperintermediate layer. Also, both the gas pressure and deposition rate maybe changed in forming the lower and upper intermediate layers.

According to the present invention, an oxide granular type perpendicularmagnetic recording medium provides both high media S/N and goodcorrosion resistance by selective combination of a Ru or Ru alloyintermediate layer and a TaNi or TaTi alloy seed layer.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1-1 is a drawing which shows the structure of a perpendicularmagnetic recording medium according to an embodiment of the presentinvention.

FIG. 1-2 is a drawing which shows the structure of a perpendicularmagnetic recording medium according to another embodiment of the presentinvention.

FIG. 2-1 is a drawing which shows a method of manufacturing aperpendicular magnetic recording medium.

FIG. 2-2 is a drawing which shows another method of manufacturing aperpendicular magnetic recording medium.

FIG. 2-3 is a drawing which shows another method of manufacturing aperpendicular magnetic recording medium.

FIG. 2-4 is a drawing which shows another method of manufacturing aperpendicular magnetic recording medium.

FIG. 2-5 is a drawing which shows another method of manufacturing aperpendicular magnetic recording medium.

FIG. 2-6 is a drawing which shows another method of manufacturing aperpendicular magnetic recording medium.

FIG. 3 is a drawing which shows the relation between full width athalf-maximum Δθ₅₀ of the Rocking curves of the Ru (0002) diffractionpeak and pit corrosion count.

FIG. 4 is a drawing which shows the relation between Ar gas pressure andfull width at half-maximum Δθ₅₀ of the Rocking curves of the Ru (0002)diffraction peak in the formation of a lower intermediate layer.

FIG. 5 is a drawing which shows the relation among Ni content in theTaNi seed layer of a perpendicular magnetic recording medium, pitcorrosion count and media S/N.

FIG. 6 is a drawing which shows the relation among Ti content in theTaTi seed layer of a perpendicular magnetic recording medium, pitcorrosion count and media S/N.

DETAILED DESCRIPTION OF THE INVENTION

A perpendicular magnetic recording medium was prepared using a sputterapparatus (C3010) made by ANELVA. This sputter apparatus consists of tenprocess chambers and one disk load/unload chamber, where each chamber isindependently evacuated. All the chambers have an air evacuationcapacity of 6×10⁻⁶ Pa or less.

The grain boundary width of crystal grains was calculated by observing abright field image of the magnetic recording layer with a TransmissionElectron Microscope. In a bright field image of the granular medium, thecrystal grain part has a dark contrast due to strong diffractionintensity and the grain boundary (oxide) part has a bright contrast dueto weak diffraction intensity. The width of each grain boundary wascalculated by drawing a line to connect the center-of-mass positions ofneighboring crystal grains and measuring the length of a grain boundarypart on the line. Grain boundary widths of 100 or more grain boundarieswere calculated and their arithmetic average was calculated to obtain anaverage grain boundary width.

Recording/reproducing characteristics were evaluated using a spin stand.The head used for this evaluation was a head with a single-pole type(SPT) writer and a giant-magnetoresistive type (GMR) reader. Theshield-gap length is 55 nm, and the read width is 120 nm, and the writewidth is 170 nm. Read output and noise were measured under the conditionthat the relative velocity between head and medium was 10 m/s, the skewangle 0°, and the magnetic spacing about 15 nm; and the media S/N wascalculated as the ratio of isolated signal amplitude at a linear densityof 1970 fr/mm to integrated medium noise when 23620-fr/mm signals wererecorded.

Corrosion resistance was evaluated with the following procedure. First,samples were left in a high-temperature high-humidity condition (60° C.temperature and 90% relative humidity or higher) for 96 hours. Then, pitcorrosions in an area from 14 mm radius to 25 mm radius were counted andthe samples were ranked as follows. The pit corrosion count of less than50 corresponds to rank A; 50 or more and less than 200 to rank B; 200 ormore and less than 500 to rank C; and 500 or more to rank D. Forpractical use, it is desirable for the medium to provide rank B orhigher corrosion resistance.

Next, specific embodiments of the present invention will be described,referring to drawings.

Embodiment 1

As shown in FIG. 1-1, a perpendicular magnetic recording medium in thisembodiment has a structure in which a pre-coat layer 12, a soft-magneticunderlayer 13, a seed layer 14, an intermediate layer 15, a magneticrecording layer 16 and an overcoat layer 17 are stacked over a substrate11. The substrate 11 was a glass substrate with a thickness of 0.635 mmand a diameter of 65 mm. First, a Ni-37.5 at. % Ta-10 a. % Zr pre-coatlayer 12 was formed and a Co-8 at. % Ta-5 at. % Zr film with an overallthickness of 100 nm was made over it as the soft-magnetic underlayer 13.The soft-magnetic underlayer 13 consisted of two layers which wereantiferromagnetically connected through Ru. After formation of thesoft-magnetic underlayer 13, a seed layer 14 and an intermediate layer15 were formed and a 12.4 nm thick magnetic recording layer 16 of Co-17at. % Cr-14 at. % Pt alloy to which 17.5 vol % of Si oxide is added, anda 4 nm thick CN overcoat layer 17 were formed over it. Ar was used assputter gas and for forming the magnetic recording layer, oxygen wasadded at a partial pressure of 20 mPa. For forming the overcoat layer17, the film was deposited at an Ar pressure of 0.6 Pa and nitrogen wasadded at a partial pressure of 50 mPa.

For the purpose of investigating a combination of an intermediate layerand a seed layer on recording/reproducing characteristics and corrosionresistance, different samples which use different seed layer andintermediate layer combinations were prepared. The seed layer andintermediate layer thicknesses and the film deposition conditions werethe same for all the samples. The seed layer thickness and theintermediate layer thickness were respectively 1 nm and 16 nm and theseed layers were formed at an Ar gas pressure of 0.6 Pa and a depositionrate of 1 nm/s and the intermediate layers were formed at an Ar gaspressure of 2 Pa and a deposition rate of 0.3 nm/s. Table 1 shows thematerials of the seed layers and intermediate layers of the preparedsamples and the results of evaluation of their media S/N and corrosionresistance.

TABLE 1 Composition of Composition of Rank of intermediate layer seedlayer Media S/N corrosion Sample (at. %) (at. %) (dB) resistance 1-1 Tinone 12.1 B 1-2 Ti Ta 13.5 C 1-3 Ti Ta—62.5Ni 13.2 C 1-4 Ti Ta—15Ti 12.9C 1-5 Co—40Cr none 11.8 B 1-6 Co—40Cr Ta 12.8 C 1-7 Co—40Cr Ta—62.5Ni12.4 C 1-8 Co—40Cr Ta—15Ti 12.0 C 1-9 Ru—5Ti none 14.8 C 1-10 Ru—5Ti Ta16.6 D 1-11 Ru—5Ti Ta—62.5Ni 16.1 B 1-12 Ru—5Ti Ta—15Ti 16.4 B 1-13 Runone 16.0 C 1-14 Ru Ta 17.6 D 1-15 Ru Ta—62.5Ni 17.2 B 1-16 Ru Ta—15Ti17.1 B

First, taking a look at the media S/N, samples 1-9 to 1-16, which use Ruor Ru alloy for the intermediate layer, achieve higher media S/N thansamples 1-1 to 1-8, which use Ti or CoCr alloy for the intermediatelayer. As a result of measurement of sample 1-2 with a transmissionelectron microscope, the crystal grain width of its magnetic recordinglayer was 0.4 nm. On the other hand, the crystal grain boundary width ofsample 1-14, which achieves the highest media S/N, was 1.1 nm, aconsiderable increase in the crystal grain boundary width as comparedwith sample 1-2. The crystal grain boundary width of samples 1-1 and 1-3to 1-8 was measured and it was found that for samples 1-1 to 1-8, whichwere low in media S/N, the crystal grain width was all below 0.5 nm. Fora perpendicular magnetic recording medium with a granular type magneticrecording layer of oxide-added CoCrPt alloy, the width of oxide crystalgrain boundaries must be increased in order to obtain high media S/N.For this purpose, Ru or Ru alloy is suitable for the intermediate layer.

Next, the results of evaluation of corrosion resistance will bediscussed. Among samples 1-1 to 1-8, which use Ti or CoCr alloy for theintermediate layer, while the samples with no seed layer showed arelatively good corrosion resistance, the samples which use a Ta or Taalloy seed layer showed poor corrosion resistance. In any case, theproblem is that both high corrosion resistance and high S/N were notachieved due to low media S/N, as mentioned above. On the other hand,among samples 1-9 to 1-16, which use Ru or Ru alloy for the intermediatelayer and provide high media S/N, corrosion resistance ranking variesgreatly depending on the seed layer. For samples 1-10 and 1-14, whichuse a Ta seed layer, their media S/N is high but their corrosionresistance is very poor, or ranked D. It has been found that althoughthe Ta seed layer is very effective in improving the crystal grainalignment of the Ru intermediate layer and obtaining high media S/N, theproblem of corrosion resistance arises when it is combined with a Ruintermediate layer. On the contrary, samples 1-11, 1-12, 1-15 and 1-16use Ta alloy to which Ni or Ti is added, namely Ta-62.5 at. % Ni alloyor Ta-15 at. % Ti alloy, for their seed layers. The combination of aTaNi alloy or TaTi alloy seed layer and a Ru or Ru alloy intermediatelayer achieved good corrosion resistance (rank B or higher) whilemaintaining high media S/N as in the case of Ta seed layers. It can bethought that the addition of Ni or Ti to Ta in the seed layer improvedthe crystal compatibility in interfaces with the Ru intermediate layerand, as a consequence, improved the degree of adhesion between the seedlayer and the intermediate layer and corrosion resistance.

The first embodiment used a magnetic recording layer of Co-17 at. %Cr-14 at. % Pt alloy to which 17.5 vol % of Si oxide is added. Also,when the ratio of Si oxide was changed to 15 vol. % and 20 vol. % orCoCrPt alloys with different compositions, Co-15 at. % Cr-14 at. % Pt,Co-19 at. % Cr-14 at. % Pt and Co-17 at. % Cr-16 at. % Pt, were used,the same tendency as in the first embodiment was observed. For the oxideto be added to the magnetic recording layer, various materials wereexamined and as a consequence, the same tendency as in the firstembodiment was observed in Al oxide, Ti oxide, Ta oxide and B oxide. Itsuggests that when a material which allows an oxide to be producedstably and is suitable for formation of about 1 nm-wide crystal grainboundaries is added to the magnetic recording layer, the effect of thepresent invention is demonstrated clearly.

Table 2 shows the calculated results of adhesion strength for theinterface between an intermediate layer and a seed layer (indicated asinterface 1 in Table 2) and the interface between a seed layer and asoft-magnetic underlayer (indicated as interface 2 in Table 2). Thesecalculated results were obtained with molecular dynamics simulation. Forthe calculation, the material of the intermediate layer was Ru, thematerial of the soft-magnetic underlayer was Co-8 at. % Ta-5 at. % Zr,and the material of the seed layer was thus varied. The calculation wascarried out in a method disclosed in Journal of Materials Research Vol.16, pp. 1789-1794 (2001).

TABLE 2 Adhesive fracture Adhesive fracture Composition of energy ofinterface 1 energy of interface 2 seed layer (at. %) (J/m²) (J/m²) Ta1.4 1.3 Ta—62.5Ni 2.2 2.6 Ta—25Ti 2.1 2.3

When Ta-62.5 at. % Ni or Ta-25 at. % Ti was used for the seed layer, theadhesive fracture energy in any interface was almost twice higher thanwhen the Ta seed layer was used. From this simulation result, it may beconsidered that the use of a TaNi seed layer or TaTi seed layerincreased the adhesion strength in the interface between the seed layerand the soft-magnetic underlayer and the interface between the seedlayer and the Ru intermediate layer, and improved corrosion resistance.

Embodiment 2

Samples 2-1 to 2-4 (perpendicular magnetic recording media) have thesame layer constitution as sample 1-15 in the first embodiment and wereprepared under the same conditions as sample 1-15 except theintermediate layer deposition method. Samples 2-1 and 2-2 have aconstitution as shown in FIG. 1-1 and samples 2-3 and 2-4 have aconstitution as shown in FIG. 1-2. The constitution of FIG. 1-2 is thesame as that of FIG. 1-1 except the intermediate layer 15 and uses alower intermediate layer 18 and an upper intermediate layer 19 laid overit instead of the intermediate layer 15.

FIGS. 2-1 to 2-4 respectively show manufacturing methods for samples 2-1to 2-4. While samples 2-1 and 2-2 use one film deposition process toform an intermediate layer, samples 2-3 and 2-4 use different filmdeposition processes to form a lower intermediate layer and an upperintermediate layer. The thickness of the intermediate layer for samples2-1 and 2-2 was 16 nm. The thickness of the upper intermediate layer andthat of the lower intermediate layer for samples 2-3 and 2-4 were both 8nm.

Table 3 shows the following types of data for each sample: seed layermaterial; drawing number corresponding to the manufacturing method;crystal grain boundary width of the magnetic recording layer ascalculated through a transmission electron microscope; full width athalf-maximum Δθ₅₀ of the Rocking curves of the Ru (0002) diffractionpeak, measured with X-ray diffraction; media S/N; and corrosionresistance evaluation results.

TABLE 3 Crystal Rank of Composition grain corro- Manu- of seed boundaryΔθ₅₀ Media sion Sam- facture layer width (de- S/N resis- ple method (at.%) (nm) grees) (dB) tance 2-1 FIG. 2-1 Ta—62.5Ni 1.1 4.5 17.1 B 2-2 FIG.2-2 Ta—62.5Ni 0.4 3.0 14.4 A 2-3 FIG. 2-3 Ta—62.5Ni 0.5 4.1 14.9 B 2-4FIG. 2-4 Ta—62.5Ni 1.0 3.4 17.6 A 2-5 FIG. 2-5 Ta—15Ti 1.1 3.6 17.3 A2-6 FIG. 2-6 Ta—62.5Ni 1.0 3.1 16.9 A 2-7 FIG. 2-7 Ta—62.5Ni 1.0 3.517.7 A

First, taking a look at the corrosion resistance results, there wasdifference in the results of evaluation of corrosion resistance thoughall the samples used the same materials for the intermediate layer andseed layer. Samples 2-2 and 2-4 were ranked A in corrosion resistance,and their Δθ₅₀ was small, namely their crystal grain alignment was good.

A sample which has the same layer constitution as sample 2-1 wasprepared using a different film deposition process for the intermediatelayer. FIG. 3 shows the relation between the full width at half-maximumΔθ₅₀ of the Rocking curves of the Ru (0002) diffraction peak andcorrosion resistance for that sample. When Δθ₅₀ is about 4 degrees orbelow, namely crystal grain alignment is high, good corrosion resistance(rank A or higher) is achieved. This means that for improvement incorrosion resistance, not only the combination of film materials butalso crystal grain alignment are important.

Next, taking a look at the media S/N, the crystal grain boundary widthof the magnetic recording layer is small and the media S/N is low forsamples 2-2 and 2-3 whose intermediate layer or upper intermediate layerin contact with the magnetic recording layer was formed in a low gaspressure atmosphere. The reason for this may be that the intermediatelayer deposited in a low gas pressure atmosphere hardly form surfaceroughness and therefore oxide segregation to crystal grain boundaries inthe magnetic recording layer hardly occurs. From these results, in orderto achieve both high media S/N and good corrosion resistance at the sametime, the intermediate layer which is in contact with the seed layershould have high crystal grain alignment and the intermediate layerwhich is in contact with the recording layer should have a large surfaceroughness.

In order to form an intermediate layer characterized as mentioned above,the intermediate layer should consist of a lower intermediate layer andan upper intermediate layer which are formed by different methods, likesample 2-4, and the lower intermediate layer should be deposited in alow gas pressure atmosphere and provide high crystal grain alignment. Inother words, it has been found that when the Ta-62.5 at. % Ni seed layeris combined with the Ru intermediate layer and the manufacturing methodas indicated in FIG. 2-4 is employed, both high media S/N and rank Acorrosion resistance can be achieved at the same time.

Sample 2-5, which has the same layer constitution as sample 2-4 exceptthe seed layer material, was prepared by the same manufacturing methodas sample 2-4. It used Ta-15 at. % Ti for the seed layer. Like sample2-4, it has been found that when the Ta-15 at. % Ti seed layer iscombined with the Ru intermediate layer and the manufacturing method asindicated in FIG. 2-4 is employed, both high media S/N and rank Acorrosion resistance can be achieved at the same time. Even when Ru-5at. % Ti or Ru-10 at. % Co, Ru-15 vol. % SiO₂ was used for theintermediate layer instead of Ru, similar results were obtained.

Samples which are the same in the layer constitution as sample 2-4 andhave their lower intermediate layers deposited at different gaspressures were prepared and an investigation was made of the relationbetween gas pressure and the value of full width at half-maximum Δθ₅₀ ofthe Rocking curves of the Ru (0002) diffraction peak. The investigationresults are shown in FIG. 4. When the gas pressure was about 1 Pa orless, Δθ₅₀ was 4 degrees or less. Because good corrosion resistance isdemonstrated when Δθ₅₀ is about 4 degrees or less, and a gas pressure ofabout 0.3 Pa or more is needed for stable electric discharge, it isdesirable to form the lower intermediate layer at a gas pressure betweenabout 0.3 Pa and 1 Pa. In addition, in order to achieve high media S/N,the upper intermediate layer must be formed in a higher gas pressureatmosphere than the lower intermediate layer and it is desirable to usethe gas pressure for forming the upper intermediate layer which is twiceor more higher than that for forming the lower intermediate layer.

Sample 2-6 has the same layer constitution as sample 2-4 though it wasprepared by a different manufacturing method. Sample 2-6 was preparedusing the manufacturing method as shown in FIG. 2-5. The film depositionrate was changed instead of using different gas pressures for formingthe lower intermediate layer and the upper intermediate layer. When alow deposition rate is used, an effect similar to the effect of filmdeposition in a high gas pressure atmosphere is obtained, surfaceroughness easily occurs and crystal grain alignment deteriorates. On theother hand, when a high deposition rate is used, an effect similar tothe effect of film deposition in a low gas pressure atmosphere isobtained, surface roughness hardly occurs and crystal grain alignmentimproves. In sample 2-6, the lower intermediate layer was formed at ahigh deposition rate and the upper intermediate layer was formed at alow deposition rate. Like sample 2-4, sample 2-6 provided both highmedia S/N and rank A or good corrosion resistance. Even when Ru-5 at. %Ti or Ru-10 at. % Co, Ru-15 vol. % SiO₂ was used for the intermediatelayer instead of Ru, similar results were obtained.

Sample 2-7 has the same layer constitution as sample 2-4 though it wasprepared by a different manufacturing method. Sample 2-7 was preparedusing the manufacturing method as shown in FIG. 2-6. In sample 2-7, theupper intermediate layer was made in a higher gas pressure atmosphereand at a lower deposition rate than the lower intermediate layer. Sample2-7 provided media S/N and corrosion resistance (rank A) equivalent tothose of sample 2-4. Even when Ru-5 at. % Ti or Ru-10 at. % Co, Ru-15vol. % SiO₂ was used for the intermediate layer and when Ta-15 at. % Tiwas used for the seed layer, similar results were obtained.

Embodiment 3

A perpendicular magnetic recording medium in the third embodiment hasthe same layer constitution as sample 2-4 in the second embodimentexcept the seed layer material and was prepared under the samedeposition conditions as sample 2-4. In the third embodiment, the TaNialloy composition of the seed layer was different. FIG. 5( a) shows therelation between seed layer composition and pit corrosion count and FIG.5( b) shows the relation between seed layer composition and media S/N.When the TaNi alloy contained about 20 at. % Ni or more, good corrosionresistance (rank A or higher) was achieved; when it contained about 80at. % Ni or less, high media S/N was achieved. Even when Ru-5 at. % Tior Ru-10 at. % Co, Ru-15 vol. % SiO₂ was used for the intermediate layerinstead of Ru, similar results were obtained.

From the above results, it is desirable that the seed layer TaNi alloycontains Ni in the range from about 20 at. % to 80 at. % in order toachieve both high media S/N and good corrosion resistance in combinationwith a Ru or Ru alloy intermediate layer.

Embodiment 4

A perpendicular magnetic recording medium in the fourth embodiment hasthe same layer constitution as sample 2-4 in the second embodimentexcept the seed layer material and was prepared under the samedeposition conditions as sample 2-4. In the fourth embodiment, TaTialloy was used for the seed layer and its composition was different.FIG. 6( a) shows the relation between seed layer composition and pitcorrosion count and FIG. 6( b) shows the relation between seed layercomposition and media S/N. When the TaTi alloy contained about 10 at. %Ti or more, good corrosion resistance (rank A or higher) was achieved;when it contained about 40 at. % Ti or less, high media S/N wasachieved. Even when Ru-5 at. % Ti or Ru-10 at. % Co, Ru-15 vol. % SiO₂was used for the intermediate layer instead of Ru, similar results wereobtained.

From the above results, it is desirable that the seed layer TaTi alloycontains Ti in the range from about 10 at. % to 40 at. % in order toachieve both high media S/N and good corrosion resistance in combinationwith a Ru or Ru alloy intermediate layer.

Embodiment 5

A perpendicular magnetic recording medium in the fifth embodiment hasthe same layer constitution as sample 1-15 in the first embodimentexcept the intermediate layer material and was prepared under the samedeposition conditions as sample 1-15. Specifically, Ta-62.5 at. % Ni wasused for the seed layer. However, in the fifth embodiment, RuCo alloywas used for the intermediate layer. Table 4 shows the intermediatelayer materials and the results of evaluation of media S/N and corrosionresistance for prepared samples. While samples 5-1 to 5-3 demonstratehigh media S/N and at least rank B corrosion resistance, samples 5-4 and5-5, which contain more than 20 at. % Co in the intermediate layer, arelow in media S/N and corrosion resistance (rank C). When Ru—Ti andRu—SiO₂ were used for the intermediate layer, or when Ta-15 at. % Ti wasused for the seed layer, similar results were obtained.

TABLE 4 Composition of Rank of intermediate Media S/N corrosion Samplelayer (at. %) (dB) resistance 5-1 Ru—5Co 17.1 B 5-2 Ru—10Co 16.9 B 5-3Ru—20Co 16.8 B 5-4 Ru—30Co 13.1 C 5-5 Ru—40Co 12.5 C

From the above results, in order for an oxide granular typeperpendicular magnetic recording medium to achieve both high media S/Nand corrosion resistance at the same time, its intermediate layer shouldbe made of Ru alloy whose main component is Ru and it is desirable thatthe content of Ru is about 80 at. % or more.

Embodiment 6

A perpendicular magnetic recording medium in the sixth embodiment hasthe same layer constitution as sample 2-4 in the second embodimentexcept the soft-magnetic underlayer composition and seed layercomposition and thickness, and was prepared under the same depositionconditions as sample 2-4. In the sixth embodiment, Co-5 at. % Nb-10. %Zr was used for the soft-magnetic underlayer. Table 5 shows the seedlayer composition, thickness, and the results of evaluation of media S/Nand corrosion resistance for prepared samples. Sample 6-1 (comparativeexample), which has no seed layer, is poorer in corrosion resistance andlower in media S/N than samples 6-2 to 6-14. On the other hand, incomparison among samples 6-2 to 6-14, which each have a seed layer,samples whose seed layer thickness is 1 nm or more demonstrate rank Acorrosion resistance and particularly samples whose seed layer thicknessis in the range from about 1 nm to 5 nm provide high media S/N. Here,the reason for deterioration in media S/N of samples with a seed layerthickness of over 5 nm is thought to be a decline in writability due toa thicker seed layer. When Ru-5 at. % Ti or Ru-10 at. % Co, Ru-15 vol. %SiO₂ was used for the intermediate layer, or when Ta-55 at. % Ni orTa-10 at. % Ti was used for the seed layer, similar results wereobtained.

TABLE 5 Composition Seed layer Rank of of seed layer thickness Media S/Ncorrosion Sample (at. %) (nm) (dB) resistance 6- — 0 15.7 C 6-2 Ta—60Ni0.5 16.4 B 6-3 Ta—60Ni 1 17.5 A 6-4 Ta—60Ni 2 17.4 A 6-4 Ta—60Ni 3 17.6A 6-5 Ta—60Ni 5 17.5 A 6-6 Ta—60Ni 6 16.8 A 6-7 Ta—30Ni 10 16.7 A 6-8Ta—30Ni 0.5 16.2 B 6-9 Ta—30Ni 1 17.2 A 6-10 Ta—30Ni 2 17.4 A 6-11Ta—30Ni 3 17.4 A 6-12 Ta—30Ni 5 17.3 A 6-13 Ta—30Ni 6 16.9 A 6-14Ta—30Ni 10 16.8 A

From the above results, in order for an oxide granular typeperpendicular magnetic recording medium to achieve both high media S/Nand good corrosion resistance at the same time, it is desirable that thethickness of the seed layer of TaNi alloy or TaTi alloy is in the rangefrom about 1 nm to 5 nm.

It is to be understood that the above description is intended to beillustrative and not restrictive. Many embodiments will be apparent tothose of skill in the art upon reviewing the above description. Thescope of the invention should, therefore, be determined not withreference to the above description, but instead should be determinedwith reference to the appended claims along with their full scope ofequivalents.

1. A perpendicular magnetic recording medium at least comprising asoft-magnetic underlayer, a seed layer, an intermediate layer, amagnetic recording layer and an overcoat layer which are stacked over asubstrate in order, wherein said seed layer is made of TaNi alloy orTaTi alloy and said intermediate layer is made of Ru or Ru alloy;wherein the thickness of said seed layer is in the range of about 1-5nm, wherein full width at half-maximum Δθ₅₀ of the Rocking curves of theRu (0002) diffraction peak measured with X-ray diffraction is about 4degrees or less.
 2. The perpendicular magnetic recording medium asdescribed in claim 1, wherein said seed layer is made of TaNi alloywhich contains Ni in the range from about 20 at. % to 80 at. %.
 3. Theperpendicular magnetic recording medium as described in claim 1, whereinsaid seed layer is made of TaTi alloy which contains Ti in the rangefrom about 10 at. % to 40 at. %.
 4. The perpendicular magnetic recordingmedium as described in claim 1, wherein said intermediate layer is madeof Ru or Ru alloy which contains about 80 at. % Ru or more.
 5. Theperpendicular magnetic recording medium as described in claim 1, whereinsaid magnetic recording layer has a granular structure which includesmany columnar grains of CoCrPt alloy and a grain boundary layercontaining an oxide.
 6. A perpendicular magnetic recording mediumcomprising: a substrate; a soft-magnetic underlayer which is formed onsaid substrate; a seed layer of TaNi alloy or TaTi alloy which is formedon said soft-magnetic underlayer; a lower intermediate layer of Ru ormetal element-added Ru alloy which is deposited on said seed layer at afirst gas pressure; an upper intermediate layer of Ru or Ru alloy whichis deposited on said lower intermediate layer at a second gas pressurehigher than said first gas pressure; and a magnetic recording layerwhich is formed on said upper intermediate layer and has a granularstructure having many columnar grains of CoCrPt alloy and a grainboundary layer containing an oxide; wherein the thickness of said seedlayer is in the range of about 1-5 nm, and wherein full width athalf-maximum Δθ₅₀ of the Rocking curves of the Ru (0002) diffractionpeak measured with X-ray diffraction is about 4 degrees or less.
 7. Theperpendicular magnetic recording medium as described in claim 6, whereinsaid seed layer is made of TaNi alloy which contains Ni in the rangefrom about 20 at. % to 80 at. %.
 8. The perpendicular magnetic recordingmedium as described in claim 6, wherein said seed layer is made of TaTialloy which contains Ti in the range from about 10 at. % to 40 at. %. 9.A perpendicular magnetic recording medium comprising: a substrate; asoft-magnetic underlayer which is formed on said substrate; a seed layerof TaNi alloy or TaTi alloy which is formed on said soft-magneticunderlayer; a lower intermediate layer of Ru or metal element-added Rualloy which is deposited on said seed layer at a first deposition rate;an upper intermediate layer of Ru or Ru alloy which is deposited on saidlower intermediate layer at a second deposition rate lower than saidfirst deposition rate; and a magnetic recording layer which is formed onsaid upper intermediate layer and has a granular structure having manycolumnar grains of CoCrPt alloy and a grain boundary layer containing anoxide; wherein the thickness of said seed layer is in the range of about1-5 nm, and wherein full width at half-maximum Δθ₅₀ of the Rockingcurves of the Ru (0002) diffraction peak measured with X-ray diffractionis about 4 degrees or less.
 10. The perpendicular magnetic recordingmedium as described in claim 9, wherein said seed layer is made of TaNialloy which contains Ni in the range from about 20 at. % to 80 at. %.11. The perpendicular magnetic recording medium as described in claim 1,wherein said intermediate layer includes a lower intermediate layer ofRu or metal element-added Ru alloy which is deposited on said seed layerat a first gas pressure; an upper intermediate layer of Ru or Ru alloywhich is deposited on said lower intermediate layer at a second gaspressure higher than said first gas pressure.